CN101243199A - Powder metallugically manufactured steel, a tool comprising the steel and a method for manufacturing the tool - Google Patents
Powder metallugically manufactured steel, a tool comprising the steel and a method for manufacturing the tool Download PDFInfo
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- CN101243199A CN101243199A CNA2006800301426A CN200680030142A CN101243199A CN 101243199 A CN101243199 A CN 101243199A CN A2006800301426 A CNA2006800301426 A CN A2006800301426A CN 200680030142 A CN200680030142 A CN 200680030142A CN 101243199 A CN101243199 A CN 101243199A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Abstract
A steel that has been manufactured powder metallurgically and that is characterised by having a chemical composition containing, in % by weight, 1.1-2.3 C+N, 0.1-2.0 Si, 0.1-3.0 Mn, max 20 Cr, 5-20 (Mo+W/2), 0-20 Co, where the total contents of niobium and vanadium (Nb + V) is balanced in relation to the ratio between the contents of niobium and vanadium (Nb/V), such that the contents of these elements and the ratio them between lie within an area that is defined by the coordinates A, B, C in the system of coordinates in Fig 1, where A: [4.0; 0.55], B: [4.0; 4.0], C: [7.0; 0.55], and no more than 1 % in total of Cu, Ni, Sn, Pb, Ti, Zr, and Al, balance iron and unavoidable impurities from the manufacturing of the steel. The invention also relates to tools for hot working or chip removal or cold working, or an advanced machine element manufactured from the steel, as well as a method for the manufacturing of such.
Description
Technical field
The present invention relates to a kind of new steel, the prepared rapid steel of preferably a kind of powder metallurgy, the instrument that it has the grindability index of improvement and is applicable to smear removal, be preferably the instrument of coating, as gear cutting instrument, screw tap with have the head end cutter of shaving separator, this is needed big toughness and in conjunction with good hardness, particularly hot hardness.Other Application Areas is to need big toughness and be combined with hardness and the use of these instruments of the suitable intensity of using.The instrument that can mention in these are used is to be used for hot worked instrument, for example be used for extruded aluminium section punch die and be used for the hot rolled roll, the member of high level machine and compacting roll just are used for the model of stamped metal etc. or the instrument of section bar.The Another application field can also be a cold work tool, is important performance to this good grindability index and good hardness.
For the steel of the instrument that for example will be used for using at extruded aluminium section, one of its most important performance is that this steel has high tempering resistance, this means that it should be able to stand high temperature for a long time and does not lose hardness, and this hardness is from Hardening Of Steel and tempering and obtain.On the other hand, not need too high, suitable size be 50-55HRC to this hardness.
If steel is to replace being used in the high-grade mechanical component, so main performance is higher hardness and intensity and in conjunction with high tenacity and also have requirement to the strictness of uniform performance.In this case, in the hardness after the tempering generally can be scope at 55-60HRC.
The steel that is used for the instrument of the model of stamped metal etc. or section bar has higher requirement for hardness, be 60-70HRC, yet it still will be in conjunction with toughness, and also like this to the steel that is used for smear removal, as gear cutting instrument, screw tap with have the head end cutter of shaving separator.Screw tap should have the hardness of the scope of 60-67HRC, and the head end cutter should have the hardness of the scope of 62-70HRC.If steel is to be used for cold worked instrument, and similar requirement is then also arranged.
The invention still further relates to and be used for hot-work or smear removal or cold worked instrument, or the high-grade mechanical component that are equipped with by above-mentioned steel, and the method that is used to prepare them.
Prior art
One type of steel that is used for cutting operation is a rapid steel, it can obtain on market with trade name ASP 2052, it forms (weight %) with following nominal is feature: 1.6C, 4.8Cr, 2.0Mo, 10.5W, 8.0Co, 5.0V, and surplus is iron and unavoidable impurities.Another kind of rapid steel is ASP 2030, and it has nominal and consists of 1.28C, 4.2Cr, 5.0Mo, 6.4W, 3.1V, 8.5Co, and surplus is iron and unavoidable impurities.Also having another kind of rapid steel is ASP 2060, and what it had a nominal consists of 2.3C, 4.2Cr, 7.0Mo, 6.5W, 6.5V, 10.5Co, and surplus is iron and unavoidable impurities, and the unit of all the components is weight %.
The invention summary
Hope improves grindability index to being used for smear removal with the steel of instrument, because grindability index is the operation of spended time in this instrument of preparation.Therefore, task of the present invention provides a kind of novel steel, is preferably rapid steel, and it has the identical advantageous property with the steel of above-mentioned prior art, improves and the grindability index of material is existing.More particularly, this steel should have following performance:
Good grindability index under sclerosis and tempered condition,
Good toughness under sclerosis and tempered condition,
Good hardness under sclerosis and tempered condition,
High yield-point,
High fatigue strength,
High bending strength and
Good wear resistance.
The prerequisite of these and other can be realized by a kind of steel, it obtains with the powder metallurgic method preparation, and it is characterized by to have and comprise following chemical constitution, in weight %, 1.1-2.3C+N, 0.1-2.0Si, 0.1-3.0Mn, maximum 20Cr, 5-20 (Mo+W/2), 0-20Co, wherein the total content (Nb+V) with respect to ratio (Nb/V) niobium and vanadium between the content of niobium and vanadium averages out, make the content of these elements and the ratio between them be in a scope, this scope is by the coordinate A in the system of coordinates in Fig. 1, B, C determines, wherein A:[4.0; 0.55], B:[4.0; 4.0], C:[7.0; 0.55], and the total amount of Cu, Ni, Sn, Pb, Ti, Zr and Al is not more than 1%, surplus is iron and the unavoidable impurities when the preparation steel.
Description of drawings
To describe the present invention in greater detail with the description of the test carried out below with reference to appended accompanying drawing, wherein:
Shown in Fig. 1 be according to steel according to the present invention on the one hand with the total amount (Nb+V) of Nb and V with on the other hand with the relation between the ratio (Nb/V) of Nb and V content, its form with system of coordinates represents,
Shown in Fig. 2 is the synoptic diagram of the size of MX-carbide as the function of the volume part of MX-carbide,
Shown in Fig. 3 is M
6The size of X-carbide is as M
6The synoptic diagram of the function of the volume part of X-carbide,
Shown in Fig. 4 is the distribution schematic diagram of carbide size during for different heat treatment and Nb/V ratio,
Shown in Fig. 5 is for d
(111)MX-and d
(331)-0.5AM
6The plane d of X-carbide
(hkl)In spacing of lattice as the synoptic diagram of the function of Nb/V ratio,
Shown in Fig. 6 is the micro-organization chart of steel F according to the present invention after the 6th thermal treatment,
Shown in Fig. 7 be grindability index, G ratio as the functional arrangement of MX-carbide size and
Shown in Fig. 8 is the graph of a relation that speed is excavated in energy expenditure and smear metal during grinding.
Detailed Description Of The Invention
The present invention is not combined with any concrete theory, different alloy materials and the different structural elements importance in the section bar that obtains desired performance will illustrate in greater detail.Under the situation of alloy content, per-cent always provides with weight %, and under the situation of structural element, per-cent always provides with volume %, except as otherwise noted except.
Nitrogen, carbon should exist with at least 1.1% and maximum 2.3% content together, preferably at least 1.4% and maximum 2.0%, more preferably between the 1.60-1.90%, when being dissolved in the martensite with box lunch under sclerosis and tempered condition to a kind of hardness of material, it is the purpose that is suitable for it.Carbon and nitrogen should combine with niobium and vanadium and facilitate (the Nb of the primary precipitated of q.s in addition, V) the MX-carbide of X type ,-nitride ,-carbonitride, and combine with tungsten, molybdenum and chromium with the M6X-carbide of facilitating the primary precipitated that in matrix, obtains q.s ,-nitride ,-carbonitride.For simplicity, this hard phase particle is called carbide in the description of back, and what it should be understood that is, if steel contains nitrogen, the term carbide also refers to nitride and/or carbonitride so.The purpose of this carbide is to give material with its desired wear resistance.In addition, they help to make steel to have the meticulous granulous structure of carbide, because carbide can play the effect of limit grain growth.In a preferred scheme, steel contains carbon and the nitrogen between the 1.65-1.80%, the alloying element of other of itself and surplus, can make steel have the characteristic that is suitable for its purpose well when particularly silicon, chromium, vanadium and niobium combine, it can obtain by the preparation method of standard, that is to say preparation without any need for work extraordinary, but carry out according to standard method.
Usually nitrogen content is not more than 0.1%, however in the powder metallurgy technology of preparing in steel the nitrogen of the much higher content of solubilized.Therefore, this steel that is characterized as of an embodiment of described steel contains a large amount of nitrogen, and nitrogen content mostly is 2.3% most, and this can obtain by the solid phase nitriding of powder of preparation.Can replace carbon at this nitrogen in mechanically resistant material, mechanically resistant material is the part of the steel of final instrument.Advantage by replacing carbon to obtain with nitrogen is that anti-sticking mill reduces, this particularly when instrument at cohesive material, as being an advantage during operation on aluminium and some stainless steels.Steel is tempering more easily also, this means to reduce tempering temperature, and this can be favourable.The content that is lower than 1.1% carbon+nitrogen will cause inadequate hardness and wear resistance, and can cause the fragility problem greater than 2.3% content.
Content with at least 0.1% joins silicon in the steel, and to improve the flowability of steel, this is important in the melt metallurgical technology.Will easilier flow by the adding steel melt that increases silicon, this is important, to avoid the obstruction relevant with granulation.Should be at least 0.2% and more preferably be at least 0.4% for fear of the obstruction silicone content during granulating.Silicon also helps to increase the carbon activity in the embodiment of silicon alloy, silicon can exist with about 2% amount at the most.When the amount more than 2%, the fragility problem occurs, so steel should not contain the Si greater than 1.2%, because under curing condition, form big M during greater than above-mentioned content
6The risk of X-carbide and weakening hardness will be bigger, this means that more preferably limiting silicone content is not more than 1.0%.In a preferred embodiment, silicone content is between 0.55%-0.70%, and this has also confirmed to use the steel of preferred carbon content to be easy to thermal treatment except above-mentioned advantage.Meaning thus that described steel can be heat-treated in wide temperature range keeps its characteristic simultaneously, and this is favourable in the preparation.
Manganese also can mainly exist with the bottom product from metallurgical melt technology, and wherein manganese has the known effect that makes sulfur-containing impurities ineffective by forming manganese sulfide, and should exist by the content with at least 0.1% in steel for this purpose manganese.The maximum level of manganese in steel is 3.0%, yet preferred manganese content is to be limited in to be 0.5% to the maximum.In a preferred embodiment, steel contains the Mn of 0.2-0.4%.
Sulphur can be used as the preparation steel in steel bottom product exists, and when content is at most 800ppm, does not influence the mechanical property of steel.Sulphur can intentionally add as alloying element, mostly is 1% most, thereby helps to improve mechanical property and processing characteristics.In one embodiment of the invention, deliberately add sulphur, sulphur content should be between the 0.1-0.3% and manganese content should be selected than higher slightly in the scheme of non-sulphur alloy for this reason, and suitable is 0.5% to maximum 1.0%.
Phosphorus also exists as the bottom product of preparation steel in steel, when content is at most 800ppm, does not influence the mechanical property of steel.
Chromium should exist with at least 3% content in steel, is preferably at least 3.5%, so that help to make steel to obtain enough hardness and toughness when time in the matrix that is dissolved in steel after sclerosis and tempering.Chromium also can be by promoting the wear resistance of steel in the hard phase particle that is included in primary precipitated, hard phase particle mainly is M
6The X-carbide.The carbide of other primary precipitated also contains chromium, yet not in identical degree.Yet too many chromium will cause remaining austenitic risk, and it is difficult to change.By the deep freezing of material, residual austenite content can be eliminated or be minimized at least.So the content that chromium can have is limited in maximum 12%.Steel needn't contain greater than 6% chromium to obtain desired performance in the Application Areas of steel.Steel contains the Cr of 3.5-4.5% and the Cr of 3.8-4.2% most preferably in a preferred embodiment.
Molybdenum and tungsten obtain enough hardness and toughness just as chromium helps steel like that after sclerosis and tempering matrix.Molybdenum and tungsten also can be included in the M of primary precipitated
6It will promote the wear resistance of steel in the carbide of X type and so.The carbide of other primary precipitated also contains molybdenum and tungsten, yet not in identical degree.Select limit and cause suitable performance so that adapt by alloying element with other.Molybdenum and tungsten can partially or even wholly replace mutually in principle, this means that tungsten can be measured generation by the molybdenum of half, or molybdenum can be measured generation by double tungsten.Yet know that by experience approximately the molybdenum of equivalent and tungsten are preferred, because this causes in production technology or the advantage of some in heat treatment technics more specifically.The total content of molybdenum+tungsten should more preferably be not more than 15% in the scope of 5-20%.The performance that is suitable for purpose can obtain with combining of other alloying elements at the content with 9-12% (Mo+W/2).The content of molybdenum should be chosen in the scope of 4.0-5.1% in a preferred embodiment in this scope, and the content of tungsten should suitably be chosen in the scope of 5.0-7.0.The nominal content of molybdenum be 4.6% and tungsten be 6.3%.
There is the purposes that depends on steel in the selection of cobalt in steel.Usually at room temperature use or the common application that in use is not heated under the extra high temperature for steel, steel should not contain the cobalt of intentional adding so, because cobalt reduces the toughness of steel and have broken risk in instrument uses.Under this external soft annealing condition hardness will increase along with the increase of cobalt contents and when the content that is higher than about 14% instrument become and be very difficult to machining, just be difficult to rotation, grinding, drilling, sawing etc.If steel is used for smear metal cutting (chipcutting) instrument, to this hot hardness is important, then suitable therewith is to contain a large amount of cobalts, and it can have 20% content at the most in this case, but just can reach desired hot hardness under the cobalt contents of 7-14% scope.When being used in chip-removing cutting tools, should more preferably contain Co between the 8.0-10.0% and the Co of preferred especially 8.8-9.3% according to steel of the present invention.
Niobium is a kind of element that plays an important role in steel according to the present invention.Previously knownly be, add a spot of niobium, at the most 1%, can help to reduce the size of carbide, this is favourable for the toughness and the hardness of material especially.According to previously known viewpoint, niobium can replace vanadium.Yet this will influence wear resistance and material and also will be difficult to grind, if particularly the steel content that contains niobium and/or vanadium is about 4% or more for a long time.
Some is ignorant before being, at least be to be ignorant in the applicant's the knowledge, i.e. the total amount of vanadium and niobium and have relation, steel wherein between the ratio between vanadium and the niobium on the other hand on the one hand, although this carbide forms the high-content of thing, yet be to be easy to astoundingly grind.This relation has formed the basis of inventive concept and by a large amount of tests the applicant has been become clear, and these tests further describe hereinafter.According to thought of the present invention, on the one hand the total amount of niobium and vanadium should average out with respect to the ratio (Nb/V) between the content of on the other hand niobium and vanadium, and the content of these elements and the ratio between them will be in the zone of being determined by coordinate A, B in Fig. 1 system of coordinates, C.More preferably, total content of these elements (Nb+V) and the ratio between them (Nb/V) be at coordinate D, E, and the determined regional inner equilibrium of F, and more preferably at coordinate G, H, in the determined zone of I, wherein:
[(Nb+V)；(Nb/V)]
A：[4.0；0.55]
B：[4.0；4.0]
C：[7.0；0.55]
D：[4.25；0.55]
E：[4.25；3.5]
F：[6.7；0.55]
G：[4.5；0.55]
H：[4.5；3.0]
I：[6.4；0.55]
Show, although in category of the present invention the high alloy content of niobium and vanadium, the size of nascent MX-carbide can limit, this helps improving abradibility.
Show that in addition will make MX-carbide growth ground still less in different hot work operation according to steel of the present invention, the ratio of the Nb/V of steel is higher, these operations are that steel stands in preparation process, for example hot isostatic pressing (HIP:ing), forging, rolling.
Find also that under study for action between the size of the carbide that forms in steel and their total content relation is arranged, the size increase of the carbide then carbide content in steel is high more.For M
6X-and this relation of MX-carbide are effective.Research also further shows, under fixed volume part and processing parameter, and M
6The X-carbide is greater than the MX-carbide.Have a kind of given maximum sized carbide if this means the steel expectation, alloy composition can be an equilibrated so, so that the content of the MX-carbide of steel is M
6The 1.5-2 of X-carbide content doubly.
The steel that it has surprisingly been found that the alloying niobium in addition has stronger relation than the steel that does not add niobium between the content of the increase of the size of MX-carbide and MX-carbide.This result shows that the adding of niobium is just favourable when a certain maximum level of MX-carbide at the most, rather than greater than this content.
According to thought of the present invention, a kind of steel can be provided, it satisfies and high yield-point, high fatigue strength, high bending strength and the toughness that combines of wear resistance and the high request of hardness preferably, and also has the nonferromagnetic substance of improvement.If steel has the composition according to claim 1, this just can realize so, and wherein this composition has obtained balance with regard to the niobium of the total content of niobium and vanadium and certain ratio and vanadium.Therefore the total content of niobium and vanadium 4.0≤Nb+V≤7.0 that should satisfy condition, preferred 4.25≤Nb+V≤6.7, more preferably 4.5≤Nb+V≤6.4,0.55≤Nb/V≤4.0 that should satisfy condition of the ratio between niobium and the vanadium simultaneously, preferred 0.55≤Nb/V≤3.5 and more preferably 0.55≤Nb/V≤3.0.Steel should contain the Nb of 2.0-2.3% and the V of 3.1-3.4% in the most preferred embodiment.Steel should have the content of the MX-carbide that is not more than 15 volume % in addition, preferably be not more than 13 volume %, more preferably be not more than 11 volume %, wherein at least 80%, preferably at least 90%, more preferably the carbide size of at least 95% MX-carbide is not more than 3 μ m on the longest prolonging direction of carbide, preferably is not more than 2.2 μ m, more preferably no more than 1.8 μ m.With regard to M
6The composition of X-carbide-shaping element chromium, molybdenum and tungsten steel should be an equilibrated also, so that the M in steel
6The content of X-carbide is not more than 15 volume %, preferably is not more than 13 volume % and more preferably no more than 12 volume %, wherein at least 80%, preferred 90% and more preferably at least 95% M
6The carbide size of X-carbide is not more than 4 μ m on the longest prolonging direction of carbide, preferably be not more than 3 μ m, more preferably no more than 2.5 μ m.
The additional alloying element that should not contain in addition, any intentional adding according to steel of the present invention.Copper, nickel, tin and lead and carbide shaping thing are not more than 1% as the admissible total amount of titanium, zirconium and aluminium.Except these elements and above-mentioned element, steel no longer contains other element and the bottom product that gets handling of other metallurgical melts from steel except containing unavoidable impurities.
Laboratory scale experiment
Nine kinds of test materialss have been prepared altogether.The chemical constitution of these materials is listed in the table below in 1.
Table 1: the chemical constitution of the steel of check (weight %); The balance iron of normal contents and impurity
| Steel | C | Si | Mn | Cr | Mo | W | Co | V | Nb | Nb/V |
| A | 1.74 | 0.60 | 0.31 | 3.95 | 4.07 | 4.15 | 10.5 | 3.97 | 1.87 | 0.47 |
| B | 1.85 | 0.62 | 0.39 | 4.23 | 5.05 | 7.18 | 12.0 | 3.50 | 1.67 | 0.48 |
| C | 1.77 | 0.56 | 0.29 | 3.94 | 4.99 | 5.09 | 0.63 | 3.94 | 1.96 | 0.50 |
| D | 1.86 | 0.63 | 0.40 | 4.20 | 7.02 | 7.14 | 12.0 | 3.25 | 1.74 | 0.54 |
| E | 1.98 | 0.41 | 0.28 | 2.98 | 2.99 | 1.14 | 7.80 | 4.08 | 2.63 | 0.64 |
| F | 1.73 | 0.62 | 0.39 | 4.20 | 6.99 | 7.00 | 11.9 | 2.63 | 1.98 | 0.75 |
| G | 1.92 | 0.41 | 0.30 | 4.28 | 1.00 | 3.24 | 8.33 | 3.76 | 3.25 | 0.86 |
| H | 1.28 | 0.6 | 0.3 | 4 | 5 | 6.4 | 8.5 | 3.1 | - | 0 |
| I | 2.30 | 0.6 | 0.3 | 4.2 | 7.0 | 6.5 | 10.5 | 6.5 | - | 0 |
Be equipped with powder by gas atomization from steel.Each powdered steel is to solidify promptly so-called HIP/QIH by carry out the Rapid Thermal isostatic pressing in the small test sleeve pipe on bigger production casing top.From little test casing, take out sample, with several these samples of mode thermal treatment, to simulate typical working condition according to following table 2.
Table 2: the thermal treatment of the representative condition that simulation is produced in ASP technology
| Thermal treatment | Temperature (℃), the residence time (h) |
| 0 | 1150/ |
| 1 | 1150/2h+1100/12h |
| 2 | 1150/2h+1130/3h |
| 3 | 1150/2h+1130/6h |
| 4 | 1150/2h+1130/ |
| 5 | 1150/2h+1150/3h |
| 6 | 1150/2h+1100/12h+1130/6h+1150/3h |
Carbide content and size
The content of the MX-carbide in the steel of being checked and size are that the thermal treatment in the table 2 that stands according to steel changes.This just can be clear that from following table 3.
Table 3: depend on the content of the MX-carbide in the heat treated steel, the size of these carbide
| Thermal treatment | Mean sizes, all * | Mean sizes, 100 maximums | MX, volume % | Mean sizes, all * | Mean sizes, 100 maximums | MX, volume % |
| {。##.##1},* | {。##.##1},* | ||||||||
| Steel A | |
||||||||
| 0 | 0.51 | 1.07 | 7.1 | 0.48 | 0.95 | 4.7 | |||
| 1 | 0.58 | 1.28 | 7.9 | 0.55 | 1.13 | 6.4 | |||
| 2 | 0.54 | 1.19 | 7.1 | 0.49 | 0.98 | 6.2 | |||
| 3 | 0.61 | 1.37 | 8.7 | 0.59 | 1.22 | 7.4 | |||
| 4 | 0.62 | 1.43 | 9.8 | - | - | - | |||
| 5 | 0.55 | 1.18 | 7.6 | 0.57 | 1.16 | 7.6 | |||
| 6 | 0.68 | 1.60 | 10.4 | 0.70 | 1.47 | 9.2 | |||
| Steel | Steel D | ||||||||
| 0 | 0.56 | 1.18 | 7.7 | 0.47 | 0.93 | 5.6 | |||
| 1 | 0.53 | 1.18 | 7.6 | 0.55 | 1.09 | 6.4 | |||
| 2 | 0.46 | 0.91 | 6.0 | 0.49 | 0.96 | 5.8 | |||
| 3 | 0.53 | 1.14 | 8.3 | 0.57 | 1.14 | 6.5 | |||
| 4 | 0.55 | 1.30 | 8.5 | 0.62 | 1.28 | 6.8 | |||
| 5 | 0.52 | 1.09 | 8.1 | 0.54 | 1.07 | 6.5 | |||
| 6 | 0.62 | 1.39 | 10.4 | 0.69 | 1.43 | 8.5 | |||
| Steel | Steel F | ||||||||
| 0 | 0.49 | 1.10 | 6.9 | 0.42 | 0.78 | 3.6 | |||
| 1 | 0.51 | 1.09 | 6.9 | 0.45 | 0.86 | 3.7 | |||
| 2 | 0.48 | 0.98 | 6.4 | 0.42 | 0.78 | 3.3 | |||
| 3 | 0.51 | 1.04 | 6.8 | 0.48 | 0.95 | 4.6 | |||
| 4 | 0.55 | 1.25 | 8.7 | 0.51 | 1.00 | 4.7 | |||
| 5 | 0.49 | 1.04 | 7.4 | 0.46 | 0.90 | 4.5 | |||
| 6 | 0.59 | 1.28 | 8.8 | 0.54 | 1.07 | 5.5 | |||
| Steel | Steel H | ||||||||
| 0 | 0.44 | 0.86 | 5.2 | 0.39 | 1.17 | 12.6 | |||
| 1 | 0.52 | 1.07 | 6.1 | 0.68 | 1.52 | 14.1 | |||
| 2 | 0.47 | 0.91 | 5.3 | 0.60 | 1.30 | 13.2 | |||
| 3 | 0.50 | 1.04 | 6.4 | 0.62 | 1.39 | 12.0 | |||
| 4 | 0.52 | 1.06 | 6.7 | 0.69 | 1.57 | 14.5 |
| 5 | 0.50 | 1.01 | 6.5 | 0.62 | 1.38 | 13.1 |
| 6 | 0.60 | 1.16 | 8.4 | 0.76 | 1.82 | 15.9 |
| Steel I | ||||||
| 0 | 0.51 | 1.03 | 4.6 | |||
| 1 | 0.62 | 1.32 | 6.2 | |||
| 2 | 0.53 | 1.08 | 4.5 | |||
| 3 | 0.57 | 1.16 | 4.1 | |||
| 4 | - | - | - | |||
| 5 | 0.55 | 1.11 | 4.4 | |||
| 6 | 0.74 | 1.59 | 6.5 | |||
*The average carbide size that relates to all MX-carbide
*The mean sizes that relates to the carbide of 100 maximums in the zone of about 20000 μ m
Fig. 1 shows the synoptic diagram of the size of No. 6 heat treated MX-carbide.In the drawings, the steel that adds niobium marks with solid black color dots, and the steel that does not add niobium marks with circle.In the drawings as can be seen, for contain-the MX-carbide size of the steel of Nb is more much smaller than the size of the carbide in the steel that does not add Nb.
To the M in the steel that depends on the heat treated check that steel stood in the table 2
6The corresponding research of the content of X-carbide and size is listed in the table below in 4.
Add niobium with the content of maximum the size of MX-carbide is had favourable effect, the residence time and the temperature in the technology depended in its variation, such as the hot isostatic pressing under the typical temperature to rapid steel, rolling and forge.The conclusion that draws from test is to be not more than 15 volume % to having the MX-carbide content, preferably be not more than 13 volume % and more preferably no more than the steel of 11 volume %, add niobium and look like favourablely, and the adding of opposite niobium seems to cause bigger MX-carbide for the steel of the MX-carbide with major part.
Table 4: depend on the M in the heat treated steel
6The content of X-carbide and size
| Thermal treatment | M 6X, volume % | Mean sizes, 100 maximums * | M 6X, volume % | Mean sizes, 100 maximums * | M 6X, volume % | Mean sizes, 100 maximums * |
| Steel B | Steel | Steel D | ||||||
| 0 | 5.5 | 1.28 | - | - | 9.2 | 1.49 | ||
| 1 | 7.6 | 1.75 | 5.3 | 1.42 | 11.7 | 1.89 | ||
| 2 | 7.5 | 1.38 | 5.6 | 1.17 | 10.5 | 1.61 | ||
| 3 | 7.2 | 1.71 | 4.7 | 1.37 | 10.7 | 1.90 | ||
| 4 | - | - | 5.9 | 1.52 | 11.9 | 2.22 | ||
| 5 | 5.7 | 1.56 | 3.6 | 1.25 | 9.3 | 1.77 | ||
| 6 | 8.4 | 2.06 | 6.8 | 1.78 | 10.5 | 2.24 | ||
| Steel F | Steel | Steel I | ||||||
| 0 | 10.9 | 1.63 | - | - | 7.4 | 1.43 | ||
| 1 | 11.1 | 1.88 | 6.7 | 1.52 | 9.7 | 1.93 | ||
| 2 | 11.8 | 1.70 | 6.8 | 1.43 | 8.5 | 1.58 | ||
| 3 | 12.3 | 1.98 | 7.1 | 1.65 | 8.9 | 1.81 | ||
| 4 | 11.7 | 2.17 | - | - | - | - | ||
| 5 | 9.9 | 1.72 | 6.4 | 1.51 | 7.7 | 1.65 | ||
| 6 | 11.8 | 2.24 | 6.4 | 1.93 | 8.2 | 2.13 | ||
Shown in Fig. 3 be about in the table 4 through the M of No. 6 heat treated steel
6The size diagrammatic sketch of X-carbide.The steel that has added niobium is in the drawings marked by solid stain, and the steel that does not add niobium marks with circle, and as seen from the figure, the adding of Nb is not to M
6The size of X-carbide has any measurable effect.
Show in addition, steel according to the present invention is having less influence in different hot work operation aspect the MX--carbide size, the Nb/V ratio of steel is higher, and this kind hot-work is that steel during preparation experiences, for example: hot isostatic pressing, forging and rolling, as being clearly from Fig. 4.Fig. 4 show hot work operation to have about 0.6 or the steel of bigger Nb/V ratio in the few of effect of size of MX-carbide.
Fig. 5 shows MX-and M
6The plane d of X-carbide
(hkl)In spacing of lattice as the synoptic diagram of the function of Nb/V ratio.Measured (111)-spacing for the MX-carbide, and for M
6The C-carbide has been measured (331)-spacing.Be clear that at this as if the adding of niobium at M
6Spacing between the lattice in the C-carbide is influence not, and this adding that shows niobium is to M
6The composition of C-carbide is influence not.For MX-carbide linear relationship seemingly between the ratio of spacing of lattice and Nb/V increases, this shows that niobium is to be dissolved in the MX-carbide.Yet steel G departs from therewith, and this may be because form big MX-carbide (＞20 μ m) in melt before granulation takes place, and this means during more a spot of Nb is to granulation or formed afterwards MX-carbide is useful.
Microstructure
Steel according to the present invention has a kind of microstructure, its sclerosis and the tempered condition under by containing MX-carbide and M
6The martensitic organizational composition of the tempered of X-carbide, MX-carbide and M
6X-carbide uniform distribution in martensite, its by be cooled to room temperature by the austenitizing temperature between 950-1250 ℃ and under 480-650 ℃ temperature tempering obtain with hardened product.The content that should have the MX-carbide that is not more than 15 volume % according to steel of the present invention, preferably be not more than 13 volume %, with more preferably no more than 11 volume %, wherein at least 80%, preferably at least 90%, more preferably the carbide size of at least 95% MX-carbide is not more than 3 μ m on the longest prolonging direction of carbide, preferably is not more than 2.2 μ m and more preferably no more than 1.8 μ m.With regard to M
6The composition of X-carbide-shaping element chromium, molybdenum and tungsten steel should be an equilibrated also, so that the M in the steel
6The content of X-carbide is not more than 15 volume %, preferably is not more than 13 volume % and more preferably no more than 12 volume %, wherein at least 80%, preferred 90% and more preferably at least 95% M
6The carbide size of X-carbide is not more than 4 μ m on the longest prolonging direction of carbide, preferably be not more than 3 μ m and more preferably no more than 2.5 μ m.
Fig. 6 is according to steel of the present invention, just the microstructure picture of the alloy F in table 2.This photo shows the MX-carbide of equally distributed black/Dark grey and bigger slightly white/grayish M
6The X-carbide.This steel contains the MX-carbide of 5.5 volume %, and it has the mean sizes of 0.5 μ m, and wherein the MX-carbide of 100 maximums in the zone of about 20000 μ m has the mean sizes of 1.1 μ m, and the M of 11.8 volume %
6The X-carbide has the mean sizes of 1.2 μ m, wherein the M of 100 maximums in the zone of about 20000 μ m
6The X-carbide has the mean sizes of 2.2 μ m.Light areas around the MX-carbide is from etch, and not corresponding therewith thing in material in fact.
Abradibility
According to an aspect of the present invention, steel should have good abradibility.The size of above-mentioned all MX-carbide all influences the abradibility of steel, so that the particle of carbide is big more in the steel, and abradibility reduces.The abradibility of steel can its G ratio provide, and it will grind many a kind of actually tolerance to material.The G ratio of steel is that the sample (so-called white dish) of 7 * 7 * 150mm by surface grinding aluminum oxide industry disk under sclerosis and annealed condition drops to and is of a size of 2 * 7 * 150mm and measures.The volume of the steel that the G ratio grinds away with the volume of employed relatively abrasive disk usually provides.Easily the material that grinds has high G ratio, and the material that is difficult to grind is to be feature with low G ratio value.Fig. 7 represents the function of abradibility as the MX-carbide size.Be clear that to have the steel of undersized MX-carbide and the steel comparison of other MX-carbide content suitable improvement has been arranged aspect abradibility with equal volume scope.
Compare energy expenditure by during grinding, can relatively excavate the value of speed (chip excavation rate) according to the highest cutting of steel of the present invention, steel of the present invention is called PUD169, it has following composition 1.69% (C+N), 0.65% Si, 0.3% Mn, 4.0% Cr, 4.6% Mo, 6.3% W, 9.0% Co, 3.2% V and 2.1Nb, surplus is iron and impurity, and a kind of reference steel, it has following composition: 1.6 C, 4.8 Cr, 2.0 Mo, 10.5 W, 8.0 Co, 5.0 V, surplus is iron and unavoidable impurities, is called ASP2052.The results are shown among Fig. 8, and be clear that, can excavate speed with the cutting that is higher than reference material about 60% under identical energy expenditure according to steel of the present invention and grind, this viewpoint from preparation sees it is quite superior.
From according to the present invention and the steel of reference material can prepare many cutting tool teeth, it uses the TiAlN coating, promptly so-called Futura coating.This steel plate uses in test, wherein to two kinds of Materials Measurements be equivalent to the rate of cutting of one hour (1h) time limit of service.In test, use following parameter:
The radial cutting degree of depth=10mm,
Axial depth of cut=3mm,
Charging=0.1mm/ tooth, the dry method machining,
Work materials=Impax.
In test, the cutting speed that records for steel of the present invention is 83m/ minute, and is 77m/ minute for what reference material recorded, therefore this means that steel of the present invention has the performance more much better than reference material.
The experiment of pilot scale
Hardness under sclerosis and tempered condition
The variation scheme of two about 200kg, each all is to be undertaken by gas atomization and hot-isostatic pressing by steel of the present invention.The sleeve pipe of the pilot scale of about 10kg is by this powdered preparation, and testing plate takes out from sleeve pipe, to estimate the hardness after sclerosis and tempering.The variation scheme of these steel according to the present invention is applicable to be had high request but still is combined with big flexible application hardness, as be used for the press tool of models such as metal or section bar, and the steel that is used for the smear removal instrument, such as screw tap and head end cutter with shaving separator.If it is to be used for cold worked instrument, then steel is had similar demand.The chemical constitution of these steel provides in table 5.The result is illustrated in the table 6.
Table 5: according to two chemical constitutions (weight %) that change scheme of steel of the present invention; The balance iron of normal contents and impurity
| Steel | C | Si | Mn | Cr | Mo | W | | V | Nb | |
| 1 | 1.70 | 0.59 | 0.29 | 3.98 | 4.69 | 6.17 | 9.03 | 3.19 | 2.08 | |
| 2 | 1.65 | 0.54 | 0.29 | 3.95 | 4.60 | 6.03 | 8.94 | 3.15 | 2.13 |
Table 6: the hardness of steel according to the present invention when different thermal treatment, (HRC)
| Stiffening temperature (℃), residence time 2-5 minute. | |||||
| Steel | Tempering temperature TA (℃) 3 * 1h | 1150 | 1180 | 1200 | 1220 |
| 1 | 500 | 69.2 | |||
| 1 | 520 | 69.9 | 69.9 | ||
| 1 | 540 | 68.8 | 68.6 | 68.5 | |
| 1 | 560 | 68.1 | 68.4 | 67.5 | 65.6 |
| 1 | 580 | 66.3 | 66 | ||
| 1 | 600 | 62.7 | |||
| 2 | 500 | 69.7 | |||
| 2 | 520 | 69.4 | 69.7 | ||
| 2 | 540 | 67.9 | 68.2 | 68.3 | |
| 2 | 560 | 67.6 | 68.0 | 67.9 | 68.2 |
| 2 | 580 | 65.6 | 65.9 | ||
| 2 | 600 | 62.0 | |||
According to the Application Areas of steel, best hardness is to select in the hardness of 50-70HRC scope.For requiring than soft, 50-55HRC, but preferably have the more Application Areas of high tenacity, limit the content of nascent C, and the N of any existence and at least some W, V, Nb, Mo and Co, so that these content are the lower limit amount at about steel, and the selection of the austenitizing temperature between hardening period is to be lower than 1100 ℃.
For the steel that is used for hot work tools, as be used for the extruding of aluminium section bar, one of most important performance is that steel has high tempering resistance, this means that it can experience long high temperature and not lose hardness, and this steel sclerosis and tempering obtain.This hardness does not need high especially, the suitable value at 50-55HRC on the other hand.If steel is used to replace senior mechanical component, salient features is higher hardness and the intensity that combines with big toughness.Under this situation, the hardness after the tempering typically can be in 55-60HRC., typically be and heat-treat under 1150-1200 ℃ and under 550-600 ℃ tempering temperature, carry out tempering, 3 * 1h suitably under 1000-1250 ℃ austenitizing temperature for these two Application Areas steel.
Steel to the press tool that is used for models such as metal or section bar, and the steel that is used for smear removal, hardness there are higher requirement, 60-70HRC, but still to combine these instruments such as gear cutting instrument, screw tap and have the head end cutter of shaving separator with big toughness.Screw tap should have the hardness of 60-67HRC scope, and the head end cutter should have the hardness of 62-70HRC scope.If it is used for cold worked instrument, then similar demand is also arranged for steel.Compatibly under the temperature of 1000-1250 ℃ austenitizing, heat-treat for these two Application Areas steel, typically, be used for smear removal instrument for 1150-1200 ℃ be used for cold work tool for 1000-1200 ℃, and tempering under 480-580 ℃ tempering temperature, typically be 550-570 ℃, 3 * 1h and have hardness in the scope of 50-55HRC.Under the situation of the steel that contains nitrogen, tempering temperature can reduce for the above reasons.
Steel has according to following nominal composition: 1.69% (C+N) in a preferred embodiment, 0.65% Si, and 0.3% Mn, 4.0% Cr, 4.6% Mo, 6.3% W, 9.0% Co, 3.2% V and 2.1% Nb, surplus is iron and impurity.The instrument that this steel is particularly suitable for cutting is compared the abradibility that it has suitable improvement with the material of being mentioned for this reason in introduction, other performance is commeasurable.This steel has also shown compares with ASP2052 that it has the machinability of improvement.
Claims (24)
1. be used for hot worked tool steel or be used for cold worked tool steel or be used for the tool steel of smear metal machining, or be used for the steel of senior mechanical component, it, contains in weight % by powder metallurgic method preparation and it is characterized by it and have following chemical constitution:
1.1-2.3 C+N
0.1-2.0 Si
0.1-3.0 Mn
Maximum 20 Cr
5-20 (Mo+W/2)，
0-20 Co，
Wherein the total amount of niobium and vanadium (Nb+V) averages out with respect to the ratio between niobium and content of vanadium (Nb/V), and the content of these elements and the ratio between them are in the zone of being determined by coordinate A, B in Fig. 1 system of coordinates, C, wherein
A：[4.0；0.55]
B：[4.0；4.0]
C：[7.0；0.55]
And the total amount of Cu, Ni, Sn, Pb, Ti, Zr and Al is not more than 1%, unavoidable impurities when surplus is iron and system steel.
2. according to the steel of claim 1, it is characterized in that, the total amount of niobium and vanadium (Nb+V) averages out with respect to the ratio between niobium and the content of vanadium (Nb/V), and the content of these elements and the ratio between them are in the zone of being determined by coordinate D, E, F, wherein
D：[4.25；0.55]
E：[4.25；3.5]
F：[6.7；0.55]。
3. according to the steel of claim 2, it is characterized in that, the total amount of niobium and vanadium (Nb+V) averages out with respect to the ratio between niobium and the content of vanadium (Nb/V), and the content of these elements and the ratio between them are in the zone of being determined by coordinate G, H, I, wherein
G：[4.5；0.55]
H：[4.5；3.0]
I：[6.4；0.55]。
4. according to the steel of claim 3, it is characterized in that the carbon in the steel and the total amount of nitrogen are between 1.4 to 2.0%, are preferably between 1.60 to 1.90%.
5. according to the steel of claim 4, it is characterized in that the carbon in the steel and the total amount of nitrogen are between 1.65 to 1.80%.
6. according to the steel of claim 1, it is characterized in that described steel contains 0.2 to 1.2% Si, be preferably 0.4 to 0.8% Si.
7. according to the steel of claim 6, it is characterized in that described steel contains 0.55 to 0.70% Si.
8. according to the steel of claim 1, it is characterized in that described steel contains 0.1 to 0.5% Mn, be preferably 0.2 to 0.4% Mn.
9. according to the steel of claim 1, it is characterized in that described steel contains 3 to 6% Cr, be preferably 3.5 to 4.5% Cr.
10. according to the steel of claim 9, it is characterized in that described steel contains 3.8 to 4.2% Cr.
11. the steel according to claim 1 is characterized in that, described steel contains 5 to 15% (Mo+W/2), is preferably 9 to 12% (Mo+W/2).
12. the steel according to claim 11 is characterized in that, described steel contains 4.0 to 5.1 Mo and 5.0 to 7.0% W.
13. the steel according to claim 11 is characterized in that, described steel contains 4.4 to 4.9 Mo and 6.1 to 6.7% W.
14. the steel according to claim 1 is characterized in that, described steel contains 5.0 to 14.0% Co, is preferably 8.0 to 10.0% Co, 8.8 to 9.3 Co more preferably.
14. the steel according to claim 1 is characterized in that, steel contains 2.0 to 2.3% Nb and 3.1 to 3.4% V.
15. the steel according to claim 1 is characterized in that, in sclerosis, tempering under 480 to 650 ℃ tempering temperature under the temperature of 950 to 1250 ℃ austenitizings, and 3 * 1h, then it has the hardness in 50 to 70HRC scopes.
16. steel according to claim 15, it is characterized in that, it has the microstructure that is made of tempered martensite, and the content of MX-carbide is not more than 15 volume %, and wherein the carbide size of at least 80% MX-carbide is not more than 3 μ m on the longest prolonging direction of carbide; M
6The content of X-carbide is not more than 15 volume %, wherein at least 80% M
6The carbide size of X-carbide is not more than 4 μ m on the longest prolonging direction of carbide.
17. steel according to claim 16, it is characterized in that, the content of MX-carbide is not more than 13 volume %, more preferably is not more than 11 volume %, and wherein the carbide size of at least 90%, more preferably at least 95% MX-carbide is not more than 2.2 μ m and more preferably is not more than 1.8 μ m on the longest prolonging direction of carbide; M
6The content of X-carbide is not more than 13 volume %, be preferably and be not more than 12 volume %, wherein at least 90%, more preferably at least 95% M
6The carbide size of X-carbide is not more than 3 μ m and is preferably and is not more than 2.5 μ m on the longest prolonging direction of carbide.
18. one kind is used for hot-work or smear metal machining or cold worked instrument or senior mechanical component, it is characterized in that, it contains each steel of with good grounds aforesaid right requirement.
19. be used for hot worked instrument or senior mechanical component according to claim 18, it is characterized in that, described steel under 950 to 1050 ℃ the austenitizing temperature sclerosis, tempering under 550 to 600 ℃ tempering temperature, 3 * 1h, then it has the hardness in 50 to 55HRC scopes.
20. be used for smear metal machining or cold worked instrument according to claim 18, it is characterized in that, described steel is hardening and tempering under 480 to 580 ℃ tempering temperature under 1000 to 1250 ℃ the austenitizing temperature, 3 * 1h, and then it has the hardness of 60 to 70HRC scopes.
21. one kind is used to prepare the instrument that hot-work or smear metal machining or cold working uses or the method for senior mechanical component, it is characterized in that, it comprises: the preparation steel melt, the described steel melt of gas atomization is to form powdered steel, by hot-isostatic pressing is that to solidify described powdered steel almost be the tool blank of instrument net shape to form steel billet or to have to so-called HIP, it has each the chemical constitution according to claim 1-14, steel billet or tool blank are hardened under 950 to 1250 ℃ austenitizing temperature, and tempering under 480 to 650 ℃ tempering temperature, 3 * 1h, make steel have the hardness of 50 to 70HRC scopes, and microstructure is made of tempered martensite, the content of MX-carbide is not more than 15 volume %, wherein the carbide size of at least 80% MX-carbide is not more than 3 μ m, M on the longest prolonging direction of carbide
6The content of X-carbide is not more than 15 volume %, wherein at least 80% M
6The carbide size of X-carbide is not more than 4 μ m and abrasive tool base to final size on the longest prolonging direction of carbide.
22. according to claim 21 be used to prepare the instrument that hot-work or smear metal machining or cold working uses or the method for senior mechanical component, it is characterized in that described steel billet stands hot-work and/or cold working to form tool blank, sclerosis and tempering then.
23. be used for the instrument that hot-work or smear metal machining or cold working uses or the method for senior mechanical component according to the preparation of claim 21, it is characterized in that described instrument is by carrying out surface-coated as physical vapor deposition or chemical vapour deposition.
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| SE05018270 | 2005-08-18 | ||
| PCT/SE2006/050290 WO2007021243A1 (en) | 2005-08-18 | 2006-08-18 | Powder metallurgically manufactured steel, a tool comprising the steel and a method for manufacturing the tool |
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- 2006-08-18 CN CN2006800301426A patent/CN101243199B/en active Active
- 2006-08-18 KR KR1020087001681A patent/KR101333740B1/en active IP Right Grant
- 2006-08-18 JP JP2008526909A patent/JP5225843B2/en active Active
- 2006-08-18 EP EP06769668.2A patent/EP1917376B1/en active Active
- 2006-08-18 WO PCT/SE2006/050290 patent/WO2007021243A1/en active Application Filing
- 2006-08-18 BR BRPI0614983-9A patent/BRPI0614983A2/en not_active Application Discontinuation
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2007021243A9 (en) | 2007-06-14 |
| JP5225843B2 (en) | 2013-07-03 |
| CN101243199B (en) | 2011-03-30 |
| WO2007021243B1 (en) | 2007-04-19 |
| SE0501827L (en) | 2007-02-19 |
| BRPI0614983A2 (en) | 2011-04-26 |
| RU2008104934A (en) | 2009-09-27 |
| JP2009504922A (en) | 2009-02-05 |
| RU2415961C2 (en) | 2011-04-10 |
| EP1917376A1 (en) | 2008-05-07 |
| SE529041C2 (en) | 2007-04-17 |
| EP1917376B1 (en) | 2019-06-19 |
| EP1917376A4 (en) | 2017-05-17 |
| WO2007021243A1 (en) | 2007-02-22 |
| KR20080038130A (en) | 2008-05-02 |
| KR101333740B1 (en) | 2013-11-28 |
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